DE102011009817A1 - Biaxially stretched film, useful e.g. for flat ribbon cable cars, comprises a polyester, whose diol component is made up of 1,4-cyclohexanedimethanol, and dicarboxylic acid component is made up of benzenedicarboxylic acid - Google Patents

Abstract

Biaxially stretched film comprises a polyester, whose: diol component is made up of at least 80 mol.% of 1,4-cyclohexanedimethanol; and dicarboxylic acid component is made up of at least 80 mol.% of one or more benzenedicarboxylic acid and/or one or more naphthalene dicarboxylic acid, a main dicarboxylic acid component with at least 55 mol.%, which is 2,6-naphthalenedicarboxylic acid or terephthalic acid, and para-dicarboxylic acid component with at least 18 mol.%, where the para-dicarboxylic acid component is different from the main dicarboxylic acid component. Independent claims are included for: (1) biaxially oriented polyester film having a transparency of greater than 70%, an opacity of less than 90%, the transparency in the UV-A region at 370 nm of less than 30%, an elastic modulus in the direction of each film of greater than 1500 N/mm 2>, but in any film direction, the elastic modulus is greater than 5000 N/mm 2>, and a F5-value (force at 5% elongation) in each film direction of greater than 40 N/mm 2>, but in any film direction a force at 5% elongation is greater than 140 N/mm 2>, a tensile strength in each film direction of greater than 65 N/mm 2>, but in any film direction of greater than 290 N/mm 2>, a shrinkage at 150[deg] C (15 minutes) in both film directions of less than 3%, but in any film direction of less than -1% (equivalent to 1% elongation), and a dielectric strength (BDV) (50 Hz, 21[deg] C, 50 relative humidity, measured in air) of at least 40 V/mu m and a partial discharge resistance (PDV) of the following equation: PDV[V]is equal to x[V/mu m].film thickness [mu m]+y[V] with an x-value of greater than 0.75 [V/mu m]and a y-value of greater than 100 [V] and a SV-value decomposition rate of greater than -3 SV-E/hour (SV-E is equal to SV-unit); and (2) producing the film, comprising extruding one or more polymer melt through a flat nozzle, for solidification on one or more rolls, reducing and detering to largely amorphous precursor film, reheating this precursor film and biaxially stretching (orienting), thermally fixing the biaxially stretched film and then rolling, where the polymer comprises the polyester.

Description

The invention relates to a biaxially stretched film whose thickness is preferably in the range of 12 to 600 microns and which is suitable for Elektroisolieranwendungen, in particular as backside insulation of solar modules. The film consists predominantly of a polyester whose diol component consists essentially of cyclohexanedimethanol. The dicarboxylic acid component is a substantial part of a benzenedicarboxylic acid or naphthalenedicarboxylic acid; however, at least 18 mol% of the dicarboxylic acid component is composed of a dicarboxylic acid other than the benzaldicarboxylic acid or naphthalenedicarboxylic acid mainly used. These films are characterized by their good manufacturability, very good hydrolysis resistance and good electrical insulation properties. The invention further relates to a process for producing the film and to its use.

Biaxially stretched films of polyesters in the specified thickness range are well known.

In electrical insulation applications such as cables, motor insulation, or solar panel backside laminate applications, relatively long lifetimes of several years are typically required at temperatures of application to the region of the glass transition temperature of the polyester polyethyleneterephthalate (= PET) most commonly used in industrial practice. 78 ° C come. Under these conditions, the hydrolysis tendency of the polyester becomes a critical size for the service life in the application. Although influencing factors such as a low carboxyl end group content (CEG content) on the hydrolysis rate have been known for a long time (eg. US-A-3,051,212 However, the processes used in industrial practice to produce low carboxyl end-group polyester necessitate meticulous process control and subsequent solid state polymerization.

A disadvantage of such raw materials is particularly evident when - as is essential for the commercial production of polyester films for economic reasons - the production waste (also recycle or (own) Regenerat mentioned) from the film production to the highest possible proportion back into ebendiese this film production become. In the production of biaxially stretched polyester films, 1.5 to 2.5 kg of raw material are generally required for one kg of film due to the process. The remainder (0.5 to 1.5 kg / kg of film) accumulates in the form of marginal strips and film trimmings, which are chopped and then reused directly or extruded and regranulated and then reused (recycled material, (own) regenerate). In the film production and even more in the subsequent re-extrusion for regenerative production, however, the Carboxylendgruppengehalt increases sharply and thus restricts the reuse of regenerate to the necessary total renunciation of this. However, reducing the rate of hydrolysis by, for example, adjusting a low carboxyl end group content of the polyester is limited in its effect, and without further complex additive systems, the resulting films are still not sufficiently hydrolyzable for many applications, such as backside laminates in solar modules.

By choosing monomers other than ethylene glycol and terephthalic acid, the rate of hydrolysis of PET can also be significantly reduced. From polyethylene naphthalate (PEN) with naphthalenedicarboxylic acid as the monomer in place of terephthalic acid films can be obtained with a significantly reduced rate of hydrolysis, but in their applicability both by the high raw material price (about factor 5 to PET) and by the much more difficult production biaxially stretched Foils (including caused by the greatly increased glass transition temperature of about 120 to 125 ° C) are limited. In addition, z. For example, in the backside laminate of a solar module, a connection to other films of other polymers (polyester, EVA, and the like) can be made. The relatively inert nature of PEN makes the manufacture of such laminates more difficult than using other polyesters.

PCT = poly (1,4-cyclohexane-dimethylene) terephthalate is also known as a hydrolysis-stable polyester, but is not used in biaxially stretched films in practice. The reason lies in the brittleness of the material, in particular after the heat fixation of the biaxially stretched films necessary for shrinkage reduction. Therefore, PCT comes on the market mostly as PETG (= PET with cyclohexanedimethanol [CHDM] + ethylene glycol [EG] as diol monomer units, usually with more than 50 mol% EG). However, PETG is no longer stable to hydrolysis, so it is no longer suitable for the target applications (electrical insulation, especially in solar modules).

In backside laminates for solar modules, at least the outermost laminate layer should ideally have the entire laminate so high a hydrolytic stability that even after 25 years in outdoor use a sufficient insulation is present. At present, this is usually by laminates of polyvinyl fluoride (PVF) (z. B. Tedlar ^®, DuPont) and PET dissolved in which at least the laminate outside consists of Tedlar and usually the PET is located as an insulating middle layer between two Tedlarlagen. However, Tedlar and other fluoropolymers are expensive and, in the future, with the rapidly growing number of solar modules reaching the end of their service life, they will also become a major recycling problem as they are neither simply self-regenerated nor disposed of with low emissions (eg. burnt) can be.

When integrated in facades solar modules transparency of the entire module is often required to still ensure residual light through the windows behind it, or to allow the architectural design of a show through the underlying facade element. Although a high reflection of the backside insulating material is usually desired in order to increase the efficiency of the solar module, but in the cases described above, this is omitted for the reasons mentioned. Object of the present invention was to provide such transparent insulation materials, d. H. Polyester films to produce.

Specifically, the object of the present invention was to provide a polyester film with a transparency of> 70% in the preferred thickness of 12-600 microns, which avoids the disadvantages of the prior art mentioned, can be produced inexpensively and by good electrical insulation properties in particular in Use as a backside laminate of solar modules is characterized and thus suitable for general use in Elektroisolieranwendungen.

This is achieved by a biaxially stretched (= oriented) film, which consists predominantly of a polyester whose diol component is at least 80 mol%, preferably at least 95 mol% and particularly preferably at least 99 mol% of 1.4- Cyclohexanedimethanol (CHDM) exists. CHDM can be present both as cis-isomer c-CHDM, trans-isomer t-CHDM or as mixture c / t-CHDM. By "diol component" is understood according to the invention derived from a diol structure which is incorporated in the polyester chain; the derived structure bears the name of the monomeric compound, the name of the monomeric compound being used as such here, if appropriate, also alternatively and equivalently in place of the component. The higher the cyclohexanedimethanol content, the higher the hydrolysis resistance. The dicarboxylic acid component of the polyester consists of at least 80 mol% of a benzenedicarboxylic acid or / and a naphthalenedicarboxylic acid (= NDC), preferably at least 95 mol% and more preferably at least 99 mol% of a benzenedicarboxylic acid or / and a naphthalenedicarboxylic acid. By "dicarboxylic acid component" is meant, according to the invention, the structure derived from a dicarboxylic acid which is incorporated into the polyester chain; the derived structure bears the name of the monomeric compound, the name of the monomeric compound being used as such here, if appropriate, also alternatively and equivalently in place of the component. The dicarboxylic acid component in the amounts indicated above preferably consists of a benzenedicarboxylic acid. The preferred naphthalenedicarboxylic acid is 2,6-naphthalenedicarboxylic acid (2,6-NDC) and the preferred benzenedicarboxylic acid is terephthalic acid (= TA).

In a particularly preferred embodiment with good stability to hydrolysis, the dicarboxylic acid component consists of at least 55 mol% (= mainly used dicarboxylic acid component), preferably at least 60 and more preferably at least 64 mol% of one of the two preferred dicarboxylic acids and more preferably terephthalic acid.

In addition to the predominantly used dicarboxylic acid (≥ 55 mol%), there are always at least 18 mol% of at least one dicarboxylic acid other than the main one used. This can be z. Example, be 2,6-naphthalenedicarboxylic acid, when the main component is terephthalic acid and vice versa. In a particularly preferred embodiment with good hydrolytic stability and good manufacturability (low brittleness), the polyester contains at least 18.0 mol% isophthalic acid (IPA) and preferably at least 20 mol% isophthalic acid and particularly preferably at least 25 mol% isophthalic acid as further dicarboxylic acid component ( Mol% based on the totality of the dicarboxylic acid components). The higher the content of isophthalic acid, the better the film can be produced economically, since the number of breaks decreases and the edge brittleness decreases. Below 18.0 mol% IPA, productivity was unsatisfactory due to the above factors. Above 25% by mole, productivity comparable to standard PET could be achieved. The proportion of isophthalic acid should not be more than 40 mol% and better not more than 36 mol%, because then the thermal and hydrolytic stability of the films decreases significantly. Between 18.0 and 40 mol% of IPA, the polyesters can also be melted well in extruders intended for PET film production at temperatures below 300 ° C., and no melt-induced temperature rises occur in the region of the melt line, resulting in gel formation and loss of productivity ; this occurs to a greater extent below 18.0 mol%. Above 40 mol% IPA, the raw materials tend to stick in the feed zones of the extruder and to significantly increased gel formation in the extrusion.

The ranges given for IPA likewise apply to other dicarboxylic acids such as NDC, preferably 2,6-NDC, as the second component in TA as the main dicarboxylic acid or TA as the second component in NDC, preferably 2,6-NDC, as the main dicarboxylic acid. This also applies to 1,4-cyclohexanedicarboxylic acid and others, wherein TA, NDC, preferably 2,6-NDC, and IPA are the preferred dicarboxylic acids.

Other dicarboxylic acids than the above-mentioned terephthalic acid, isophthalic acid or NDC or 2,6-NDC, such as other aromatic but also aliphatic dicarboxylic acids may also be present, but usually lead to a deterioration in the production properties, or and the thermal and hydrolytic stability , Therefore, their proportion, if present at all, is preferably less than 10 mol% and ideally less than 1 mol%.

As described above, TA is the most preferred dicarboxylic acid. In a preferred embodiment, in addition to TA, at least 5 mol%, preferably at least 10 mol% NDC, preferably 2,6-NDC, are present, with more than 25 mol% less preferred, and ideally, 21 mol% NDC, or 2.6-NDC, should not be exceeded. Apart from TA and NDC, preferably 2,6-NDC, in a particularly preferred embodiment, IPA is still present in the amounts described above. The higher the content of NDC, or 2,6-NDC, the higher the mechanical strength of the resulting films. An increasing NDC / 2,6-NDC content continues to have a positive effect on the hydrolysis resistance. However, as the NDC / 2,6-NDC content increases, raw material costs also increase and manufacturability becomes more difficult.

The said polyesters can - if they are not commercially available - for example, by the known DMT process or by the TPA process are prepared, as explained in more detail below in the description of the preparation of the masterbatches. The corresponding diols and dicarboxylic acids (TPA process) or their lower alkyl esters (DMT process) are reacted in the stated molar amounts.

The film contains as main ingredient a polyester. The film is preferably at least 70 wt .-% and particularly preferably 95 wt .-% of a polyester, wherein inorganic fillers are neglected. The remaining at most 30 wt .-% may be other polymers such as polypropylene or other organic fillers such as UV stabilizers or flame retardants (the wt .-% refer to the mass of the total film, wherein inorganic fillers are neglected).

The aforementioned polyesters may contain other monomers in addition to the above-mentioned main monomers. Other diols are z. Ethylene glycol (EG), propylene glycol (PG), 1,4-butanediol, diethylene glycol (DEC), neopentyl glycol and others. The proportion of diols other than CHDM is less than or equal to 20 mol%, preferably less than or equal to 5 mol%, and ideally less than or equal to 1 mol%. The higher the cyclohexanedimethanol content, the higher the hydrolysis resistance.

The film according to the invention may further contain inorganic or organic particles needed to adjust the surface topography or appearance (gloss, haze, etc.). Such particles are z. Calcium carbonate, apatite, silica, titania, alumina, cross-linked polystyrene, cross-linked polymethyl methacrylate (PMMA), zeolites and other silicates such as aluminum silicates. These compounds are generally used in amounts of 0.01 to 5 wt .-%, preferably 0.02 to 0.3 wt .-%, and in particular 0.03 to 0.15 wt .-% (based on the weight of Foil). Particularly preferred are calcium carbonate and in particular silicon dioxide.

The particle sizes d _{50 used} are generally between 0.02 and 8 μm and preferably between 0.1 and 5.5 μm and particularly preferably between 0.3 and 2.5 μm in order to achieve good running safety in production. Fiber-shaped inorganic aggregates such as glass fibers are unsuitable because they make the production of the polyester film uneconomical due to many breaks. The lower the d ₅₀ value of the particles used, the higher the partial discharge resistance (see below). If particles with a d ₅₀ of above 8 μm are used, the preferred partial discharge strengths can no longer be reliably achieved.

The high transparency according to the invention is achieved, in particular, if the proportion of particles with a d ₅₀ of> 3 μm is less than 0.5% by weight and in particular if the proportion of particles with a d ₅₀ of> 3 μm is smaller is 0.1% by weight based on the weight of the film. The highest transparency values are achieved when using silica.

The transparency of the film is greater than 70% and preferably greater than 75%, in particular> 85% and ideally> 88%. The haze of the film is preferably less than 90%, particularly preferably <50%, in particular <35% and ideally <7%. The higher the transparency and the lower the turbidity, the better the suitability of the film for those solar modules, which should still have a residual light incidence through behind windows, or allow in the context of architectural design, a shine through the underlying facade element, with diminishing haze improves the view through the module so that clear images are visible. High turbidity leads, in particular in glazing applications, to a diffuse light incidence. This may be desirable in individual cases, but it is usually not.

To achieve a high transparency and low haze according to the invention, multilayer embodiments of the film according to the invention have proven to be particularly favorable. The above-mentioned particles for optimizing the processing properties are supplied to both or particularly preferably only one outer layer and are then found in the other layers only in a smaller amount, as z. B. would be expected via a Regenerateintrag. The thickness of the particle-containing cover layer / cover layers is / are preferably less than 50% of the total film thickness, more preferably less than 30%, in particular less than 25% and ideally <15% of the total film thickness. In a preferred embodiment, the particle-containing cover layer / cover layers has a content of the abovementioned particles of less than 2% by weight, in particular less than 1% by weight and in particular less than 0.5% by weight. % based on the total weight of the affected stratum.

In addition to the additives mentioned, the film may additionally contain further components such as flame retardants (preferably organic phosphoric acid esters) and / or UV stabilizers and heat stabilizers. A selection of suitable UV stabilizers can be found in FR 2812299 , Particular preference is given to UV stabilizers which act as UV absorbers, in particular triazine-based, since in particular these have sufficient long-term stability (in solar modules usually more than 20 years) or a product from the HALS group (hindered amine light stabilizers). , which additionally protect the oxidatively sensitive polymers with a high cyclohexanedimethanol content, mostly without even appreciably absorbing UV light. A combination of triazine and HALS has proved to be particularly favorable, wherein instead of the triazine, a UV absorber from another product group, such as. As benzotriazoles or benzophenones, can be used. UV stabilizers are added in a preferred embodiment between 0.1 and 5% by weight (based on the total weight of the layer to which they are added), the effective minimum level of UV absorber and HALS being 0.1% by weight each. %, so that a combination of both products always results in at least 0.2% by weight in the layer in question. In the case of strong UV exposure (direct unprotected tanning, or indirect tanning over several years), the proportion of UV absorber + HALS should be at least 1 wt .-% in the most exposed layer. Addition of stabilizer to a layer below the layer facing the light source, according to experience, no longer leads to any appreciable improvement in the UV stability. Therefore, in the case of multilayer films, an addition, in particular, into the layer (s) below the cover layer (s) containing the UV stabilizer does not occur at all, or only via the entry via regenerate, ie preferably less than 60% and particularly preferably less than 30 % of the weight percent of stabilizer contained in the topcoat (s). An example of the present invention can be used stabilizers from the group of UV absorbers is the commercially available Tinuvin ^® 1577 (manufacturer BASF formerly Ciba SC Switzerland; 2- (4,6-diphenyl-1,3,5-triazin-2-yl) - In the case of the compounds from the HALS group, in particular polymeric or oligomeric stabilizers having a molecular weight of> 500, more preferably> 900 and ideally> 1300 have proven to be particularly suitable, for example methylated reaction products of N, N '-bis (2,2,6,6-tetramethyl-4-piperidinyl) -1,6-hexadiamine polymers with morpholine-2,4,6-trichloro-1,3,5-triazine (CAS NUMBER 193098-40-7 above) which -ZV-3529 are sold by Cytec, USA and are particularly preferred within the meaning of the invention. the polymeric and oligomeric HALS result in lower concentrations than lower molecular weight stabilizers in an effective stabilizing and result in films with better commercially ^® as Cyasorb electrical property s.

When using the abovementioned stabilizers in the stated amounts, the transparency of the films according to the invention in the UV-A range at 370 nm is <30% and preferably <10% and particularly preferably less than 5%.

Furthermore, it has proven to be advantageous if the film is added to a stabilizer in the form of a radical scavenger, since thereby the thermal long-term stability can be improved. Advantageously, the film according to the invention contains such radical scavengers or heat stabilizers in amounts of 50 to 15,000 ppm, preferably 100 to 5000 ppm, particularly preferably 300 to 1000 ppm, by weight the foil. The stabilizers usually added to the polyester raw material are arbitrarily selected from the group of primary stabilizers such as sterically hindered phenols or secondary aromatic amines or the group of secondary stabilizers such as thioethers, phosphites and phosphonites and zinc dibutyl dithiocarbamate or synergistic mixtures of primary and secondary stabilizers. The phenolic stabilizers are preferred. The phenolic stabilizers include, in particular, sterically hindered phenols, thiobisphenols, alkylidenebisphenols, alkylphenols, hydroxybenzyl compounds, acylaminophenols and hydroxyphenylpropionates (corresponding compounds are described, for example, in US Pat "Plastic Additives", 2nd Edition, Gächter Müller, Carl Hanser-Verlag , and in "Plastics Additives Handbook", 5th Edition, Dr. Ing. Hans Zweifel, Carl Hanser-Verlag ). Particularly preferred are the stabilizers having the following CAS numbers: 6683-19-8, 36443-68-2, 35074-77-2, 65140-91-2, 23128-74-7, 41484-35-9, 2082-79 -3, and Irganox ^® 1222 from Ciba Specialties, Basel, Switzerland, in particular embodiments, the types ^® Irganox 1010, Irganox ^® 1222, Irganox ^® 1330 and Irganox ^® 1425, or mixtures thereof are preferred.

The film according to the invention is generally produced by extrusion processes which are known per se and is single-layered or multi-layered.

The film thickness is between 12 and 600 microns and preferably between 25 and 350 microns and more preferably between 35 and 300 microns. Below 12 μm, sufficient electrical insulation for the target applications, in particular solar modules, is generally not achieved, and production is becoming increasingly difficult. From 300 microns, the breaking strength decreases significantly and above 600 microns this is too low for the target applications.

The particles and the other additives are preferably introduced into the corresponding layer via a masterbatch. For the preparation of the masterbatch particle / additive and polyester are preferably mixed in a multi-screw extruder and extruded through a hole die and granulated (= extrusion masterbatch).

However, the particles or / or additives can also be added directly during the production of polyester in order to produce a masterbatch or batch raw material (= polycondesification material batch). In the case of the DMT process (DMT = dimethyl terephthalate as starting monomer), the particles / additives are usually added after the transesterification or directly before the polycondensation (eg via the transport line between transesterification and polycondensation vessel) as dispersion in cyclohexanedimethanol. The addition can also be done before the transesterification. In the case of the TPA process (TPA = terephthalic acid = terephthalic acid as starting monomer), the addition is preferably carried out at the beginning of the polycondensation. However, a later addition is also possible. It has proven advantageous in this method, when the dispersion is filtered in cyclohexane prior to the addition of a PROGAF ^® PGF 57 filter (Hayward / Indiana, USA).

From the technical properties ago, z. As the agglomeration, offer the Polykondensationsmasterbatche an advantage. For short-term adjustments, small or variable batch sizes, the extrusion masterbatch has advantages in terms of flexibility over polycondensation masterbatches.

Also possible is the metering of the particles or additives directly in the film production in the extruder. However, this often has the disadvantage that the homogeneity compared to the other two methods is worse and agglomerates may occur, which may adversely affect the film properties.

In the process for producing the films according to the invention, it is expedient to proceed by extruding the corresponding polymer melts optionally equipped with particles / additives through a flat die, the film thus obtained for solidification on one or more rolls as a substantially amorphous prefilm is peeled off and quenched, then the film is reheated and biaxially stretched (oriented) and the biaxially stretched film is heat set.

It has proved to be favorable if the temperatures in the entire extrusion do not exceed 295 ° C. and preferably do not exceed 285 ° C. and ideally 280 ° C., since otherwise there will be marked gelation in the film. This leads u. a. to breaks in the manufacturing process and to a deterioration of the electrical properties.

The best properties in terms of hydrolytic stability and electrical properties are obtained when the raw materials are melted and extruded in a twin-screw extruder. Become Single screw extruder used, the raw materials should be dried before the extrusion. This is conveniently carried out at temperatures between 110 and 155 ° C, for a period of 20 minutes to 1.5 hours. Longer times and higher temperatures lead to a thermal degradation of the polymers used.

The biaxial stretching is generally carried out sequentially. In this case, it is preferable to stretch first in the longitudinal direction (that is, in the machine direction = MD direction) and then in the transverse direction (that is, perpendicular to the machine direction = TD direction). This leads to an orientation of the molecular chains. The stretching in the longitudinal direction can be carried out with the help of two according to the desired stretch ratio at different speeds rolling. For cross-stretching you generally use a corresponding clip frame.

The temperature at which the stretching is carried out may vary within a relatively wide range and depends on the desired properties of the film. In general, the longitudinal and also the transverse extension at T _g + 5 ° C to T _g + 50 ° C (T _g = glass transition temperature of the polymer with the highest T _g in the used (co-) polyester) is performed. It has proved to be beneficial for the productivity when temperatures between T _g + 5 ° C to T _g + 20 ° C are set.

The closer the films are stretched to the glass transition temperature, the lower the edge embrittlement observed in the process, which can lead to breaks. The longitudinal stretch ratio is generally in the range of 2.0: 1 to 6.0: 1, preferably 2.7: 1 to 4.5: 1. The transverse stretch ratio is generally in the range of 2.0: 1 to 5.0: 1, preferably 3.1: 1 to 4.6: 1, and that of an optionally performed second longitudinal and transverse extension is 1.1: 1 to 5 , 0: first

The longitudinal stretching may optionally be carried out simultaneously with the transverse extension (simultaneous stretching).

In the subsequent heat-setting, the film is held for about 0.1 to 10 seconds at a temperature of 170 to 255 ° C, preferably 210 to 250 ° C, and ideally at a temperature of 220 to 240 ° C. The actual (from the film) experienced temperatures are usually 1 to 3 ° C below the set in the fixing frame air temperatures. The temperature set in the fixing process (= air or ambient temperature) can not be measured directly on a finished film. But it can be determined from the finished film in which as in US6737226 Column 6 described, the actually experienced fixing temperature is determined and added to this 1 to 3 ° C. The result indicates a bandwidth for the fixing temperature set in the process.

Subsequently, or beginning in the heat-setting, the film is optionally relaxed by 0.5 to 15%, preferably by 2 to 8%, in the transverse and optionally also in the longitudinal direction and then cooled and wound in the usual manner.

In order to achieve the desired good electrical insulation properties, it has proven to be favorable if the area stretching ratio (longitudinally transverse) is greater than 5, or better still greater than 7 and particularly preferably greater than 8. The surface stretch ratio is in a preferred embodiment below 17. A surface stretch ratio above 20 has proved to be unfavorable in terms of running safety of the film and from an area stretch ratio of 24, it is difficult to achieve economically interesting run lengths of the film web.

The surface stretch ratios mentioned lead to films which preferably have in each film direction an modulus of greater than 1500 N / mm ² and particularly preferably in each film direction of greater than 2000 N / mm ² and ideally in each film direction of greater than 2300 N / mm ² and preferably does not have an E-modulus greater than 5000 N / mm ² in any direction of the film and, ideally, no modulus of elasticity greater than 4000 N / mm ² in any direction of the film.

The F5 value (force at 5% elongation) is preferably greater than 40 N / mm ² in each film direction and particularly preferably greater than 50 N / mm ² in each film direction and ideally greater than 60 N / mm ² in each film direction; Preferably, the film in no direction of the film has a force at 5% elongation of greater than 140 N / mm ² .

The tear strength is preferably greater than 65 N / mm ² in each film direction and particularly preferably greater than 75 N / mm ² in each film direction and ideally greater than 85 N / mm ² in each film direction is preferably in no foil direction at greater than 290 N / mm ² and more preferably in no foil direction at> 220 N / mm ² and ideally in no foil direction at> 190 N / mm ² .

Compliance with said mechanical values is extremely useful for good handling of the film in the downstream processing operations (cutting, wrapping, laminating, stacking, etc.). High mechanical strengths prevent stretching and folding in subsequent processes. At the mentioned upper limits, the risk of partial overstretching (overstretching) of the film in the production process begins, which leads to lower breaking strength and strongly fluctuating properties in the overstretched regions. The mechanical strengths are also significantly influenced by the IPA content in addition to the draw ratios. Strengths generally decrease with increasing IPA content and above 40 mole% IPA, it becomes difficult to achieve the preferred values (stretch ratios must be greatly increased, resulting in many breaks in the process). Below 20 mol%, and in particular below 18 mol% IPA, the risk of partial overstretching (overstretching) of the film in the production process increases if the desired values are to be achieved.

The transparency of the film increases with increasing IPA content.

The stretch ratios mentioned also lead to films which have sufficient elongation at break to be flexible enough in the backside insulation of solar modules for the mechanical loads during production and in the application (eg wind load). The elongation at break should be greater than 20% in each film direction and is preferably greater than 45% in each film direction and ideally greater than 75%. To achieve these elongation at break values, it has proven to be advantageous if the area stretch ratio is less than 24 and better less than 17. With increasing IPA content, the elongation at break increases.

In a preferred embodiment, the shrinkage of the films according to the invention at 150 ° C. (15 min) in both film directions is below 3%, more preferably below 2.5% and ideally in both film directions below 1.9%. The shrinkage in the transverse direction is preferably <1.0%, particularly preferably <0.75% and ideally <0.1%. The shrinkage is preferably in no film direction <-1.0% (corresponding to 1.0% elongation), more preferably in no film direction <-0.75% and ideally in no film direction <-0.5%. This can be achieved by setting the (ambient = air) temperature in the fixation greater than 210 ° C. and preferably greater than 220 ° C., and particularly preferably greater than 228 ° C. The relaxation in the transverse direction is preferably above 3% and preferably at least 30% of this relaxation is carried out at temperatures below 200 ° C. The low shrinkage is particularly important for use in the back side insulation or in back side laminates of solar modules, since the laminating process higher temperatures occur, which at higher shrinkage values lead to greater film losses and also can generate waves and wrinkles. The film must be laminated to the solar module at high shrinkage values, especially in the transverse direction with overhang. When laminating the film then shrinks and any remaining supernatants must be cut off. A significantly negative shrinkage (stretching) for waves and wrinkles on the solar module and thus to significant sorting of finished solar modules.

The two most important electrical properties of the films according to the invention are the Breakdown Voltage (BDV) and the Partial Discharge Voltage (PDV). Of particular importance is above all the BDV.

The films according to the invention have a BDV (50 Hz, 23 ° C., 50 relative air humidity, measured in air) of at least 40 V / μm, preferably of at least 100 V / μm and ideally of at least 190 V / μm.

The partial discharge strength PDV follows the following equation: PDV [V] = x [V / μm] · film thickness [μm] + y [V]

Films according to the invention preferably have x values of> 0.75 [V / μm] and y values of> 100 [V], particularly preferably x> 1 [V / μm] and y> 200 [V] and very particularly preferably x> 1.5 [V / μm] and y> 300 [V].

These electrical properties are achieved when the diol and dicarboxylic acid components of the polyester are in mol% in the range according to the invention. The electrical properties are achieved with particular reliability, if the mechanical properties in the preferred and better in the particular preferred ranges are, especially if moduli of elasticity and tear strengths do not exceed the said preferred upper limits. For achieving the desired electrical properties, it has also proven to be favorable if set fixing temperatures of 210 ° C not exceeded and 250 ° C are not exceeded.

The life of polyester-based polymeric electrical insulating materials is significantly affected by environmental conditions such as heat and relative humidity. A failure criterion of the polyester after aging under certain humidity and temperature criteria may be that the film used becomes brittle and brittle over time and then water can penetrate, which leads to a negative influence on the electrical properties or even endangers the desired Elektroisolierwirkung. In applications in which the electrical insulating film additionally contributes to the mechanical strength of the overall composite, this property is also lost after aging.

The cause of failure in the case of polyesters is often the hydrolytic cleavage of the polyester chains, wherein from a certain minimum chain length, the brittleness of the film is so large that it mechanical stresses such. B. stretching or bending no longer withstands.

As a measure of the chain length and thus also of the hydrolytic degradation behavior or hydrolysis resistance, the standard viscosity (SV) (which is related to η _rel , see below) was determined as a function of the aging time. For this purpose, the film samples in an autoclave at 110 ° C and 100% rel. Humidity conditioned and the SV value checked after regular times.

In a preferred embodiment, the SV is above 750 before the beginning of the measurement, more preferably above 800, and ideally above 850. A high chain length at the beginning is advantageous since it prolongs the service life at the same rate of degradation of the polymer used. Chain lengths corresponding to an SV of <600 are to be avoided since only very short lifetimes can be achieved. Chain lengths that are too high above an SV of 1200 are also to be avoided, since this can lead to problems in the extrusion, which adversely affect the process capability and thus the economic usability.

As a measure of the degradation rate, the SV value is plotted against time in the autoclave and the slope of the regression line is determined. The autoclaving conditions are explained in more detail in the section Measuring Methods. A preferred embodiment has a slope of> -3 SV-E / h (SV-E = SV unit) under the conditions described in the section Measuring Methods, a particularly preferred one has a slope of> -2 SV-E / h and ideally the slope at> -1 SV-E / h. A slope of <-4 SV-E / h is to be avoided in any case, since the deterioration of the material properties progresses too fast. A slope greater than or equal to 0 is also problematic because of material changes in the end use that are very different from the current standard (PET as a spacer film) and thus can lead to difficulties in laminate stability.

The inventively good low SV degradation rates are achieved when the diol and dicarboxylic acid components of the polyester in mol% in the range according to the invention, in particular, exceeding these upper limits for IPA and EG is unfavorable. The SV degradation rates will continue to be positively impacted independently of the above, if the film is made according to the described process parameters.

Films containing the polymer system according to the invention are outstandingly suitable for electrical insulation applications, especially when exposed to a long service life (years) and higher temperatures (> 60 ° C) and humidity (more than 10% relative humidity), since they have their good electrical Properties obtained even under moist heat conditions for a long time. Such applications are z. B. ribbon cables in automobiles, cables in seat heaters, motor insulation and especially the backside insulation in solar modules.

The film can be both alone, as well as a laminate with other films, eg. As EVA or PE films are used.

The polyester films according to the invention and the other films contained in the laminates are bonded by means of suitable adhesives which are applied both from solutions and as a hotmelt to the film according to the invention or to the respective other film. The films are then glued between two rolls to form a composite. Suitable adhesives must be according to the respective film type to be selected. Polyester-based adhesives, acrylates and other industrial adhesive systems have proven suitable. Preferably, polyurethane-based adhesives are used. Two-component adhesive systems are particularly preferred. These consist of polyurethane prepolymers with isocyanate end groups, which can be crosslinked with polyfunctional alcohols. The isocyanate end groups can either aromatic nature, such as. As diphenylmethane diisocyanate (MDI) or toluene diisocyanate (TDI), or aliphatic nature, such as. Hexamethylene diisocyanate (HDI) or isophorone diisoyanate (IPDI). The above components are blended with an excess of isocyanate groups along with other components such as stabilizers, particles, among others, as well as organic solvents to obtain the required properties such as tack, dryness of the surface of the adhesive, solids content, as well as color adjustment. The adhesive mixture can cure either at room temperature or at elevated temperature. The surface of the carrier layer, or / and the surfaces of the opposite side can be physically pretreated to produce an optimal adhesive bond. Suitable methods are both the corona pretreatment and a flame treatment, as well as a plasma pretreatment. The corona treatment is preferably employed, with partial oxidation resulting in increased polarity of the surface of the material.

The laminate produced in this way, or the individual layer of foil according to the invention, must then still be bonded to the embedding material of the solar cells during the production of the solar module. The most commonly used potting material in industrial practice is ethylene vinyl acetate (EVA); In addition, other materials such as polymethylmethacrylate (PMMA), polyvinylbutyral (PVB) and many others occur.

In principle, the same isocyanate adhesives can be used for bonding to the embedding materials as for bonding the laminate layers. If the films according to the invention represent the outer layer to the embedding medium of the cells (as described above, usually EVA), it is generally possible to dispense with adhesives since, surprisingly, the films according to the invention already have good adhesion properties to the usual embedding materials (in particular to EVA and PVB ) exhibit. A physical pretreatment as described above additionally improves the adhesion. The adhesion to the embedding media can also be improved by applying a coating. Inline coating during the film production process after the longitudinal stretching and before the transverse stretching again proved to be particularly economical, since no additional operation is required.

This coating has excellent durability against moisture and elevated temperature and is therefore suitable for use as a back cover in solar modules. It shows good mechanical resistance and withstands the loads occurring in the film production process, the winding and unwinding of the film as well as in the production of the solar modules without damage.

In a preferred embodiment, a coating consisting of a polyurethane and a crosslinker is applied to the film according to the invention as adhesion promoter, as described, for example, in US Pat WO 2010/094443 ,

When polyethylene (PE) or polypropylene films (PP) are used as laminate components, adhesives can usually be dispensed with. Again, a physical pretreatment as described above is advantageous.

The film according to the invention / or. The laminate containing this film is applied to the embedding medium in the production of the solar modules and pressed with this by known methods.

In the following exemplary embodiments, the measurement of the individual properties takes place in accordance with the cited standards or methods.

measurement methods

Standard viscosity (SV)

The standard viscosity SV is - based on DIN 53726 - Measured by the measurement of the relative viscosity η _{rel of} a 1 wt .-% solution in dichloroacetic acid (DCE) in a Ubbelohde viscometer at 25 ° C. From the relative viscosity η _rel . the dimensionless SV value is determined as follows: SV = (η _rel. -1) × 1000

shrink

The thermal shrinkage is determined on square film samples with an edge length of 10 cm. Samples are cut with one edge parallel to the machine direction and one edge perpendicular to the machine direction. The samples are measured accurately (the edge length L ₀ is determined for each machine direction TD and MD, L _{0 TD} and L _{0 MD} ) and annealed for 15 min at the specified shrinkage temperature (here 150 ° C) in a convection oven. The samples are taken and measured accurately at room temperature (edge length L _TD and L _MD ). The shrinkage results from the equation Shrink [%] MD = 100 * (L _{0 MD} - L _MD ) / L _{0 MD} Shrink [%] TD = 100 * (L _{0 TD} - L _TD ) / L _{0 TD}

Measurement of the transparency at 370 nm

The transparency is measured with a Lambda 3 UV / Vis spectrometer from Perkin Elmer.

Measurement of dielectric strength / dielectric strength (BDV)

The measurement of the dielectric strength is carried out according to DIN 53481-3 (taking into account DIN 40634 for the special film instructions). It is by means of ball / plate (electrode diameter 49.5 mm) at a sinusoidal AC voltage of 50 Hz at 21 ° C and 50 rel. Humidity measured in air.

Measurement of partial discharge strength (PDV)

The PDV is going to IEC 60664-1 certainly

Measurement of the mean particle diameter d ₅₀

The determination of the mean particle diameter d ₅₀ was carried out by laser on a Master Sizer (Malvern Instruments, UK) according to the standard method (other measuring devices are, for example, Horiba LA 500 (Horiba Ltd., Japan) or Helos (Sympatec GmbH, Germany). which use the same measuring principle). The samples were placed in a cuvette with water and then placed in the meter. The measuring process is automatic and includes the mathematical determination of the d ₅₀ value. By definition, the d ₅₀ value is determined from the (relative) cumulative curve of the particle size distribution: the point of intersection of the 50% ordinate value with the cumulative curve gives the desired d ₅₀ value on the abscissa axis.

Measurement of the mechanical properties of the film

The determination of the mechanical properties is carried out after DIN EN ISO 527-1 to 3 ,

Haze and transparency

The haze and transparency will diminish ASTM-D 1003 measured by haze-gard plus from BYK-Gardner GmbH, Germany, without compensation.

autoclaving

The foils (10 × 2 cm) are hung on a wire in the autoclave (Adolf Wolf SANOklav type: ST-MCS-204) and the autoclave is filled with 2 l of water. After closing the autoclave, it is heated. At 100 ° C, the air is displaced by the water vapor through the drain valve. This is closed after about 5 minutes, after which the temperature rises to 110 ° C and the pressure to 1.2-1.5 bar. After the set time (at least 12 h), the autoclave is automatically switched off and the foils are removed after opening the drain valve. At these then the SV value is determined.

Examples

Method: The raw materials were mixed and extruded in a twin-screw extruder from Japan Steel Works with degassing. In the extruder zones and in the melt line, the maximum temperature was 275 ° C. The throughput was 2000 kg per hour. The melt was extruded through a slot die (temperature 275 ° C) on a chill roll (30 ° C) and then stretched by a factor of 3.2 in the longitudinal direction at 105 ° C and then by a factor of 3.2 in the transverse direction at 110 ° C. stretched.

The film was then fixed at 222 ° C with 2% transverse relaxation set in the last field. In the two following fixing fields 190 ° C and 150 ° C were set and the relaxation here was another 3%. The total residence time in the fixation was 15 s.

In 1 an optional layer structure of a film according to the invention is shown.

The figure shows a three-layered film whose preparation is described in Example 1, with the base layer B (1), the cover layer A (2) and the cover layer A '(3). The two outer layers A and A 'z. B. each be 10 microns thick and the base layer 255 microns.

Raw materials used:

• R1 = polycyclohexanedimethanol terephthalate isophthalate, type Durastar DS2000 (manufacturer Eastman, USA) SV = 980, IPA content about 26 mol%, TA content about 74 mol%
• R2 = Raw material R1 with 1% by weight Sylysia 320 from Fuji Silysia (Japan), compounded in a twin-screw extruder from Japan Steel Works with degassing, SV = 900
• R3 = Raw material R1 with 10% by weight of Tinuvin 1577 (manufacturer BASF formerly Ciba SC, Switzerland), compounded in a twin-screw extruder from Japan Steel Works with degassing, SV = 870
• R4 = raw material R1 with 10% Cyasorb-ZV-3529 (manufacturer Cytec, USA), compounded in a twin-screw extruder from Japan Steel Works with degassing, SV = 870
• R5 = PETG type Esstar 6763 (manufacturer Eastman, USA), SV = 1045, TA content 100 mol%, ethylene glycol content about 69 mol%, cyclohexanedimethanol content about 31 mol%

To produce the film according to Example 1, the raw material R1 was used for the base layer B and the raw materials R1, R2, R3 and R4 for the cover layers A / A '(see Table 1).

Comparative example

For the preparation of the film according to Comparative Example 1, the raw material R5 was used (monofilm), s. Table 1.

The film properties can be found in Table 1. property example 1 Comparative Example 1 Raw materials f. base layer R1 100% by weight R5 100% by weight Raw materials f Coex layers A / A ' R1 75% by weight R2 5% by weight R3 10% by weight R4 10% by weight total thickness in μm 275 50 SV value of the film directly after production - 913 919 Hydrolysis rate after 144 h in an autoclave in SV / h -0.77 -4.1 Shrink along in % 1.7 shrink cross in % 0.0 E-module along in N / mm2 2600 E-module across in N / mm2 2600 Force at 5% stretch along in N / mm2 71 Force at 5% stretch in N / mm2 70 Tear strength along in N / mm2 102 Tear strength along in N / mm2 105 Elongation at break along in % 97 Elongation at break across in % 94 Dielectric strength / dielectric strength (EDP) in V / μm 197 Partial discharge strength (PDV) in V 1006 transparency in % 88 cloudiness in % 10

QUOTES INCLUDE IN THE DESCRIPTION

This list of the documents listed by the applicant has been generated automatically and is included solely for the better information of the reader. The list is not part of the German patent or utility model application. The DPMA assumes no liability for any errors or omissions.

Cited patent literature

• US 3051212 A [0003]
• FR 2812299 [0024]
• US Pat. No. 6,737,226 [0040]
• WO 2010/094443 [0067]

Cited non-patent literature

• "Kunststoffadditive", 2nd Edition, Gächter Müller, Carl Hanser-Verlag [0026]
• "Plastics Additives Handbook", 5th Edition, Dr. Ing. Hans Zweifel, Carl Hanser-Verlag [0026]
• DIN 53726 [0071]
• DIN 53481-3 [0074]
• DIN 40634 [0074]
• IEC 60664-1 [0075]
• DIN EN ISO 527-1 [0077]
• 3 [0077]
• ASTM-D 1003 [0078]

Claims (15)

Biaxially stretched film, consisting predominantly of a polyester whose Diol component consists of at least 80 mol% of 1,4-cyclohexanedimethanol (CHDM) and its Dicarboxylic acid component consists of at least 80 mol% of one or more benzenedicarboxylic acid (s) or / and one or more naphthalenedicarboxylic acid (s), the dicarboxylic acid component of a - Main dicarboxylic acid component having at least 55 mol% proportion, which is selected from one of the two dicarboxylic acids 2,6-naphthalenedicarboxylic acid and terephthalic acid, and from a - Sub-dicarboxylic acid component having at least 18 mol% proportion, wherein the secondary dicarboxylic acid component is different from the main dicarboxylic acid component. A film according to claim 1, characterized in that the dicarboxylic acid component consists of one or more benzene dicarboxylic acid (s). A film according to claim 1 or 2, characterized in that the naphthalenedicarboxylic acid is 2,6-naphthalenedicarboxylic acid (2,6-NDC) and the benzenedicarboxylic acid is terephthalic acid (= TA). A film according to claim 1, 2 or 3, characterized in that the main dicarboxylic acid component is terephthalic acid. A film according to any one of claims 1 to 4, characterized in that the secondary dicarboxylic acid component 2,6-naphthalenedicarboxylic acid is when the main dicarboxylic acid component is terephthalic acid, and Terephthalic acid is when the main dicarboxylic acid component is 2,6-naphthalenedicarboxylic acid. A film according to any one of claims 1 to 4, characterized in that the secondary dicarboxylic acid component is isophthalic acid (IPA). Film according to one of claims 1 to 6, characterized in that the secondary dicarboxylic acid component has a content of at least 20 mol%, preferably at least 25 mol%. Film according to one of claims 1 to 7, characterized in that the film contains inorganic or organic particles, preferably in an amount of 0.01 to 5 wt .-% (based on the weight of the film), wherein the particles particularly preferably a Particle size (d ₅₀ ) of 0.02 to 8 microns have. A film according to any one of claims 1 to 8, characterized in that the film contains one or more additives selected from the group: flame retardants, UV stabilizers, heat stabilizers (= radical scavengers) and mixtures thereof. Film according to one of claims 1 to 9, characterized in that the film thickness is between 12 and 600 microns. Film according to one of claims 1 to 10, characterized in that the transparency of the film is greater than 70% and / or the haze of the film is less than 90%. Biaxially oriented polyester film, characterized by - a transparency of greater than 70% and - a haze of less than 90% and - a transparency in the UV-A range at 370 nm of <30% and - an E-modulus in each foil direction of greater than 1500 N / mm ² , but in no film direction has an modulus of greater than 5000 N / mm ² , and - an F5 value (force at 5% elongation) in each film direction greater than 40 N / mm ² , but none Film direction a force at 5% elongation of greater than 140 N / mm ² , and - a tear strength in each film direction greater than 65 N / mm ² , but in no film direction greater than 290 N / mm ² , and - a shrinkage at 150 ° C. (15 min) in both film directions of less than 3%, but in no film direction of <-1.0% (corresponds to 1% elongation), - a dielectric strength (BDV) (50 Hz, 21 ° C, 50 relative humidity, measured in air) of at least 40 V / μm and a partial discharge strength (PDV) of the following equation: PDV [V] = x [V / μm] · film thickness [μm] + y [V] with an x-value of> 0.75 [V / μm] and a y value of> 100 [V] and - an SV value degradation rate of> -3 SV-E / h (SV-E = SV- Unit). A process for the production of a film according to claim 1, wherein one or more identical or different polymer melts is extruded through a flat die, stripped to solidify on one or more roll (s) as a largely amorphous prefilm and quenched, then this billet is reheated and biaxially stretched ( oriented) and the biaxially stretched film heat-set and then rolled up, characterized in that the polymer consists of a polyester whose Diol component to at least 80 mol%, consisting of 1,4-cyclohexanedimethanol (CHDM) and its Dicarboxylic acid component consists of at least 80 mol% of one or more benzene dicarboxylic acid (s) or / and one or more naphthalene dicarboxylic acid (s), wherein the dicarboxylic acid component of a - Main dicarboxylic acid component having at least 55 mol% proportion, which is selected from one of the two dicarboxylic acids 2,6-naphthalenedicarboxylic acid and terephthalic acid, and from a - Sub-dicarboxylic acid component having at least 18 mol% proportion, wherein the secondary dicarboxylic acid component is different from the main dicarboxylic acid component. Use of a film according to claim 1 for electrical insulation applications, in particular for flat cable in automobiles, cables in seat heaters and as motor insulation. Use of a film according to claim 1 for the backside insulation in solar modules.

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